Lead and arsenic free optical lanthanum borate glass

ABSTRACT

The present invention describes lead and arsenic free and preferably gadolinium and further preferably also fluorine free optical glasses for the application fields mapping, projection, telecommunication, optical communication engineering, mobile drive and/or laser technology with a refractive index of 1.75≦n d ≦1.85, an Abbe number of 34≦v d ≦44 and have a low transformation temperature, namely lower than or equal to 560° C. and preferably lower than or equal to 550° C., as well as good producability and processability and crystallisation stability. The glasses according to the present invention within the following composition range (based on oxide in % by weight) contain the following components:  
                                           SiO 2     0.5-8           B 2 O 3     10-25         ZnO   10-26         La 2 O 3     18-34         Ta 2 O 5     &gt;15-25           Nb 2 O 5     0.5-15          WO 3      0-10         Al 2 O 3     0-2         Li 2 O   0-5         Na 2 O   0-6         K 2 O   0-8         Cs 2 O   0-9         MgO   0-5         CaO   0-5         SrO   0-5         BaO   0-5         Y 2 O 3      0-10         TiO 2     0-6         ZrO 2      0-11         HfO 2     0-6         Σ B 2 O 3 , ZnO   30-45         Preferably Σ La 2 O 3 , Ta 2 O 3 ,   &gt;50         Nb 2 O 3 , Y 2 O 3 , ZrO 2           Σ Alkali oxides    0-15         Σ Alkaline-earth oxides    0-15         Σ Al 2 O 3 , Y 2 O 3 , WO 3 , TiO 2 ,    0-15         ZrO 2 , Hf 2 O 3 , Alkaline-earth oxides                                                        
In addition, they also may contain conventional refining agents.

The present invention relates to a lead and arsenic free and preferably gadolinium free and fluorine free optical lanthanum borate glass, to the use of such a glass in the fields of mapping, projection, telecommunication, optical communication engineering, mobile drive and laser technology, as well as to optical elements respectively preforms of such optical elements.

In the recent years, the tendency on the market in the field of optical technologies as well as opto-electronic technologies (application fields mapping, projection, telecommunication, optical communication engineering, mobile drive and laser technology) goes more and more into the direction of miniaturization. This can be seen with the finished products which become smaller and smaller and naturally requires an increasing miniaturization of the single structural members and components of such finished products. For the producers of optical glasses, this development means a clear decrease of the demanded volumes of rough glass in spite of increasing quantities of finished products. At the same time, there is an increasing pricing pressure from the side of the reprocessors to the producers of glass, since with the production of such smaller components made of block and/or ingot glass noticeably more waste will be produced proportionally based on the product and for the processing of such miniature parts a higher operating expense is necessary than for larger structural members.

Instead of the removing of glass portions for optical components from block or ingot glass which is common till today, therefore recently production procedures become important in which directly after the glass melt preforms respectively pills which are as close as possible to the final contour respectively geometry such as e.g. gobs or spheres may be yielded. For example, the reprocessors' requests for preforms which are close to the final geometry for re-pressing, so-called “precision gobs”, are increasing. Normally, these “precision gobs” preferably mean completely fire-polished, free or half-free formed glass portions which are already portioned and have a geometry which is close to the final form of the optical component.

Such “precision gobs” may preferably also be converted into optical elements such as lenses, aspheres etc. by the so-called “precise pressing” or “precise molding” process. Then, a further processing of the geometric form or the surface with e.g. a surface polish is no longer required. This procedure can comply with the smaller volumes of melted glass (distributed on a high number of small parts of material) in a flexible way by shorter set-up times. Because of the relatively lower number of parts per time unit and the normally smaller geometries, the creation of value cannot be caused by the value of the material alone. Rather, the products have to leave the press in a state ready for installation, i.e. laborious post-processing, cooling and/or cold re-processing must not be necessary. Because of the required high accuracy of geometries, precision instruments with high grade and therefore expensive mold materials have to be used for such a pressing procedure. The lifetimes of such molds massively affect the profitability of the products and/or materials produced. A very important factor for a long lifetime of the molds is a working temperature which is as low as possible, but which can only be lowered to a point at which the viscosity of the materials to be pressed is yet sufficient for the pressing procedure. This means, that there is a direct relationship between the processing temperature and therewith the transformation temperature Tg of a glass to be processed and the profitability of such a pressing process: The lower the transformation temperature of the glass, the longer the lifetimes of the molds; and therefore the higher the earnings. Thus, there is a demand for so-called “low-Tg-glasses”, i.e. glasses having low melting points and transformation temperatures, i.e. glasses with a viscosity at temperatures which are as low as possible which is sufficient for processing.

Further, from a process technical point of view of the melt there is a growing demand for “short” glasses, i.e. glasses having a viscosity which varies strongly within a certain viscosity range at a relatively small change in temperature. This behaviour has the advantage in the melting process that the times of hot forming, i.e. the closure times of the molds, can be decreased. Because of that, on the one hand the throughput will be increased, i.e. the cycle times will be reduced. On the other hand, because of that also the mold material will be protected which also has a positive effect on the total production costs, as described above. Such “short” glasses have the further advantage that also glasses with higher tendency to crystallization may be processed by the faster cooling than with corresponding longer glasses. Therewith prenucleation which could cause problems in succeeding steps of secondary hot forming will be avoided. This presents the possibility that such glasses may also be stretched to fibres.

Furthermore it is also desirable that, besides the mentioned and the required optical properties, the glasses are sufficiently chemically resistant.

The prior art already describes glasses with similar optical state or with a comparable chemical composition, but these glasses have immense disadvantages. In particular, many of the glasses contain higher proportions of Gd₂O₃ which as a rare-earth oxide has a weak band at 590 nm and thus deteriorates the internal transmittance, and/or components which increase the tendency to crystallization, such as e.g. TiO₂.

US 2003/0211929 relates to an optical glass for precisely pressed products having a Tg of lower than 630° C. The latter property is achieved by the addition of a very high amount of B₂O₃ and ZnO. In every case, the glass contains Gd₂O₃ in a proportion of at least 5% by mol.

JP 2003/201142 describes an optical glass for precisely pressed products having also a low Tg. Here also this property is achieved by the addition of a very high amount of B₂O₃ and ZnO. In every case, the glass contains Gd₂O₃ in a proportion of at least 6% by weight.

US 2003/0191008 comprises an optical glass with a high refractive index for the precise pressing technology. The glass contains very high proportions of Nb₂O₃ of at least 30% by weight. Nb₂O₅ in such high proportions deteriorates the internal transmittance of the glass.

JP 2003/238198 describes an optical glass for precisely pressed products having a low Tg. The latter property is achieved by the addition of LiF and/or ZnF, wherein in every case fluorine is contained as a component in an amount of at least 9% by weight. Fluorine is disadvantageous with respect to a stable melting and production process, in particular because of the strong evaporation.

JP 2003/300751 describes a low melting glass for precisely pressed products. The low Tg of 480 to 580° C. is i.a. achieved by the addition of Bi₂O₃. In every case, Bi₂O₃ is contained and imparts self-color to the glass which deteriorates the internal transmittance of the glass.

JP 2002/173336 describes a low melting phosphate glass having a high dispersion respectively low Abbe number of 20 to 32.

DE 35 34 575 relates to a glass for eye glass lenses which in every case comprises a component for coloration. Here, lanthanum oxide is only an optional component.

DE 36 05 668 relates to an optical tellurite glass which in every case comprises toxic tellurium oxide as a component.

DE 101 26 554 describes borosilicate glasses with very high refractive indexes.

The documents EP 1 236 694 A1, US 2003/0100433 and US 2003/0211929 describe optical glasses which are lead and fluorine free, but which in every case contain Gd₂O₃.

JP 60-221338 relates to glasses which in every case contain lithium oxide as a component and in which at least a part of one oxide is replaced by fluorine.

The object of the present invention is, to provide an optical glass with which desired and advantageous optical properties (n_(d)/v_(d)) with concurrent low transformation temperatures can be realized, in particular also by virtue of ecological considerations without the use of PbO and As₂O₃ and preferably also without the components Gd₂O₃ and fluorine. This glasses should further be processible by precise pressing and should be suited for the application fields mapping, projection, telecommunication, optical communication engineering, mobile drive and laser technology, should have a refractive index n_(d) of 1.75<n_(d)≦1.85, an Abbe number v_(d) of 35≦v_(d)≦44 and preferably a transformation temperature which is as low as possible of Tg≦560° C. The meltability and processability of them should also be well, as well as they should have sufficient crystallization stability which makes a production in continuously conducted aggregates possible. A glass within a viscosity range of 10^(7.6) to 10¹³ dPas which is as “short” as possible is desirable. With a so-called short glass generally a glass is meant which within the viscosity range of 10² to 10¹³ dPas has a very steep viscosity curve. For the glasses according to the present invention the term “short” should belong to the viscosity range of 10^(7.6) to 10¹³ dpas.

The above object is solved by the embodiments of the present invention which are described in the patent claims.

In particular, a lead and arsenic and preferably gadolinium and fluorine free optical glass having a refractive index n_(d) of 1.75≦n_(d)≦1.85 and an Abbe number v_(d) of 34≦v_(d)≦44 is provided which comprises the following components (based on oxide in % by weight): SiO₂ 0.5-8   B₂O₃ 10-25 ZnO 10-26 La₂O₃ 18-34 Ta₂O₅ >15-25   Nb₂O₅ 0.5-15  WO₃  0-10 Al₂O₃ 0-2 Li₂O 0-5 Na₂O 0-6 K₂O 0-8 Cs2O 0-9 MgO 0-5 CaO 0-5 SrO 0-5 BaO 0-5 Y₂O₃  0-10 TiO₂ 0-6 ZrO₂  0-11 HfO₂ 0-6 Σ B₂O₃ + ZnO 30-45 Σ Alkali oxides  0-10 Σ Alkaline-earth oxides 0-8 Σ Al₂O₃, Y₂O₃, WO₃, TiO₂, ZrO₂,  0-15 HfO₂, Alkaline-earth oxides Conventional refining agents 0-2

Preferably the sum of the oxides La₂O₃+Ta₂O₃+Nb₂O₃+Y₂O₃+ZrO₂ is higher than or equal to 50% by weight based on oxide.

Preferably the glasses are free of components which are not mentioned,

The glasses according to the present invention have the same optical state, such as the Abbe number and the refractive index, as known optical glasses of similar glass families. However they are featured by good meltability and processability, low production costs due to reduced processing costs, as well as a good environmental compatibility.

In particular, these glasses are suitable for processing close to the final contour, such as e.g. the production of precision gobs, as well as for a blank pressing process (precise pressing) for producing an optical component with accurate final contour. In this context, preferably the viscosity-temperature-profile and the processing temperature of the glasses according to the present invention were adjusted, so that such a hot forming close to the final geometry respectively contour is also possible with sensitive precision apparatuses.

In addition, the combination of crystallization stability and viscosity-temperature-profile of the glasses according to the present invention may make a thermal (further) treatment (pressing respectively re-pressing) of the glasses with nearly no problems possible.

In particular, the glasses according to the present invention have a refractive index n_(d) of 1.75≦n_(d)≦1.85, preferably of 1.78≦n_(d)≦1.83, especially preferred of 1.80 to 1.81, an Abbe number of 34≦V_(d)≦44, preferably of 36≦v_(d)≦43, preferably of 39≦v_(d)≦43, especially preferably of 40≦v_(d)≦42.

According to an embodiment of the present invention the glasses according to the present invention have a transformation temperature Tg≦560° C., preferably Tg≦550° C.

According to the present invention a so-called “low-Tg-glass” means a glass with a low transformation temperature Tg, i.e. preferably a Tg of at most 560° C.

Preferably, the glasses according to the present invention are as “short” as possible within a viscosity range of 10^(7.6) to 10¹³ dPas. In this case “short glasses” mean glasses with a strong variation in the viscosity within a certain viscosity range at a relatively small change of the temperature. Preferably, the temperature interval ΔT in which the viscosity of this glass falls from 10^(7.6) to 10¹³ dPas is at most 100° K.

FIG. 1 shows the viscosity curve of a glass according to the present invention according to example 10. In FIG. 1 the vertical lines show the temperature interval ΔT in which the viscosity of this glass varies from 10^(7.6) to 10¹³ dPas. Here, ΔT is between 542 and 637° C., i.e. it is 95° K.

FIG. 2 shows a transmission curve of a glass according to the present invention according to example 19. The wavelengths at which the transmission is 5% and 80% are shown. From those a color code of 38/32 follows.

The “internal quality” according to the present invention means that the glass has a proportion of bubbles and/or streaks and/or similar defects which is as low as possible respectively preferably that it does not at all contain anything like this.

In the following the term “X free” respectively “free of a component X” means that the glass substantially does not contain this component X, i.e. that such a component is present in the glass only as an impurity, but that it is not added to the glass composition as a single component. In this case, X is an arbitrary component, such as for example Gd₂O₃.

In the following all data of the proportions of the glass components are in % by weight and based on oxide, unless otherwise stated.

The base glass system of the glass according to the present invention is the lanthanum borate system which has intrinsically a good basis for the desired properties.

The glass according to the present invention has a proportion of ZnO of at least 10% by weight, preferably of at least 12% by weight, especially preferred of at least 14% by weight, as well as a proportion of B₂O₃ of also at least 10% by weight, preferably of at least 15% by weight, especially preferably of 17% by weight, and it is therefore a well-melting low-Tg-glass. The proportion of ZnO is at most 26% by weight, preferably at most 24% by weight, especially preferably at most 22% by weight. ZnO contributes to the desired viscosity-temperature-behaviour (“short” glass) in the viscosity range of 10^(7.6) to 10¹³ dPas.

The maximum proportion of B₂O₃ is 25% by weight, preferably at most 24% by weight, especially preferably at most 23% by weight. The strongly network-forming properties of B₂O₃ increase the stability of the glasses against crystallization and the chemical resistance. However, the proportion show not exceed 25% by weight, since then the glasses become “longer”, which is also not preferable according to the present invention. In addition, during the melting and melting-on process parts of the added B₂O₃ may evaporate which makes an accurate adjustment of the composition difficult.

The sum of the proportions of ZnO and B₂O₃ is at least 30% by weight, preferably at least 33% by weight, further preferred 34% by weight, especially preferably 38% by weight. A reduction of ZnO and B₂O₃ to a content of lower than 30% by weight would lead to glasses which could not be featured by the term “low-Tg-glass”. The sum of B₂O₃ and ZnO is at most 45% by weight, preferably at most 42% by weight, especially preferred at most 41% by weight. A further increase to above 45% by weight would reduce the refractive index too much. Suited ranges for the sum of ZnO and B₂O₃ are 30 to 45% by weight, 34 to 42% by weight, 38 to 41% by weight or 33 to 41% by weight.

Besides B₂O₃, SiO₂ is contained in these glasses as a network-forming agent in an amount of at least 0.5% by weight, preferably of at least 1% by weight, especially preferred of 2% by weight. The maximum proportion of SiO₂ is 8% by weight, preferably 7% by weight, especially preferred 6% by weight. An increase of the proportion of SiO₂ to above 8% by weight would result in the increase of the transformation temperature to above 560° C. and to a reduction of the refractive index.

The glass according to the present invention has a proportion of La₂O₃ of at least 18% by weight, preferably of at least 20% by weight, preferably of at least 21% by weight, especially preferably of at least 23% by weight. The proportion of La₂O₃ is limited to at most 34% by weight, preferably at most 33% by weight, especially preferably at most 32% by weight. The mentioned upper limit of 34% by weight should not be exceeded, because otherwise the viscosity of the glass will be increased too much. The minimum proportion should not fall below 20% by weight, to ensure the high refractive index.

The glass according to the present invention has a proportion of Ta₂O₅ of at least >15% by weight, preferably of at least 15.5% by weight. The maximum proportion of Ta₂O₅ is 25% by weight, preferably at most 24% by weight, especially preferably at most 20% by weight. The mentioned upper limit of 25% by weight should not be exceeded, since otherwise the glass becomes too expensive and thus it is not economical any longer. The minimum proportion should not fall below >15% by weight, to ensure the high refractive index with a concurrent high Abbe number.

The glass according to the present invention has a proportion of Nb₂O₅ of at least 0.5% by weight, preferably of at least 1% by weight, especially preferably of 2% by weight. The maximum proportion of Nb₂O₅ is 15% by weight, preferably at most 10% by weight, further preferably at most 8% by weight, especially preferably at most 7% by weight. The given upper limit of 15% by weight should not be exceeded, since Nb₂O₅ imparts light self-color to the glass and thus the internal transmittance of the glass will be deteriorated. Furthermore, a higher proportion than 15% by weight of Nb₂O₅ results in a too strong decrease of the Abbe number. The minimum proportion should not fall below 0.5% by weight, to ensure the high refractive index.

WO₃ may be incorporated into the glass up to a proportion of a maximum of 10% by weight, preferably of 5% by weight. WO₃ serves to adjust the refractive index and the Abbe number. The glass can be free of WO₃ what is most preferred according to particular embodiments of the invention.

Y₂O₃ may be contained in the glass from 0 to a maximum of 10% by weight, preferably up to 9% by weight, especially preferably up to 8% by weight. Like WO₃, it serves for adjusting the optical state.

Especially preferred, the glass is free of TiO₂ and HfO₂. They may be contained in an amount of 0 to a maximum of 6% by weight, preferably up to a maximum of 3% by weight. Both components contribute to high refractive indexes and high dispersions, as well as result in increased Tgs and viscosities of the glass. Furthermore, TiO₂ affects the transmission by absorption in UV and the crystallization behaviour in a negative way.

Preferably, the glass according to the present invention is free of ZrO₂ but may contain at least 1% by weight, preferably at least 2% by weight. The maximum proportion of ZrO₂ is 11% by weight, preferably at most 10% by weight, especially preferably at most 9% by weight. The given upper limit of 11% by weight should not be exceeded, because such high proportions of ZrO₂ in the glass result in enhanced devitrification.

The glasses according to the present invention contain Li₂O as alkali metal oxide in a maximum amount of 5% by weight, preferably at most 4% by weight, further preferably 3% by weight. Suited are also amounts are also 2% by weight, 1% by weight or even low amounts such as 0.1% by weight. A suited range is for example 0.1 to 4% by weight. The glass may optionally be free of LiO.

The glass according to the present invention contains at most 6% by weight, preferably at most 5% by weight, especially preferably at most 4% by weight of Na₂O.

The glass according to the present invention contains at most 8% by weight, preferably at most 7% by weight, especially preferably at most 6% by weight of K₂O.

If the glass contains caesium oxide, it is contained in amounts of at most 9% by weight, preferably of at most 8% by weight and further preferably of at most 7% by weight.

The sum of alkali metal oxides in the glass according to the present invention is 0 to 10% by weight. Preferable are at most 7% by weight, especially preferable are at most 6% by weight. The sum of alkali metal oxides is at most 10% by weight, which value should not be exceeded, since otherwise the refractive index in such a glass system decreases too strong. The addition of the alkali metal oxides serves to optimize the melting-on behaviour, i.e. they act as fluxing agent. In addition, they serve to reduce the Tg.

For a flexible regulation of the viscosity-temperature-behaviour the glass according to the present invention may optionally contain alkaline-earths (MO), which are selected from the group consisting of MgO, CaO, SrO and/or BaO. This sum MO is at most 8% by weight, preferably at most 5% by weight and most preferably at most 4% by weight.

The glass according to the present invention contains at most 2% by weight, preferably at most 1.5 and especially preferably at most 1% by weight of Al₂O₃.

The glass according to the present invention as an optical glass is preferably also free of coloring and/or optically active, such as laser active, components.

In particular, the glass according to the present invention is preferably also free of components which are redox-sensitive, such as for example Ag, and/or free of toxic respectively deleterious components, such as for example the oxides of Tl, Te, Be and As. In every case, the glass is free of PbO and arsenic.

According to an embodiment of the present invention, the glass according to the present invention is preferably also free of other components which are not mentioned in the patent claims, i.e. according to such an embodiment, the glass substantially consists of the mentioned components. Here, the term “substantially consisting of” means that other components are present only as impurities, but are not deliberately added to the glass composition as a single component.

The glass according to the present invention may contain conventional fining agents in low amounts. Preferably, the sum of the fining agents added is at most 2.0% by weight, more preferably at most 1.0% by weight. As a fining agent at least one of the following components may be contained in the glass according to the present invention (in % by weight, in addition to the rest of the glass composition): Sb₂O₃ 0-1 and/or SnO 0-1 and/or SO₄ ²⁻ 0-1 and/or F⁻  0-1.

Also fluorine and fluorine-containing compounds tend to evaporation during the melting and melting-on process and thus make an accurate adjustment of the glass composition difficult. Therefore, the glass according to the present invention preferably is also free of fluorine.

Further, the present invention relates to the use of the glasses according to the present invention in the application fields mapping, projection, telecommunication, optical communication engineering, mobile drive and laser technology.

Further, the present invention relates to optical elements which comprise the glass according to the present invention. In this case, optical elements in particular may be lenses, aspheres, prisms and compact structural members. In this case, according to the present invention the term “optical element” comprises also preforms of such an optical element, such as for example gobs, precision gobs and the like.

In the following, the present invention is explained in detail by a series of examples. But the present invention is not limited to the mentioned examples.

EXAMPLES

Tables 2 to 5 in example 2 contain embodiment examples within the preferable composition range. The glasses which are described in the examples were prepared as in example 1:

Example 1

The raw materials for the oxides are weighed out, one or more fining agents, such as e.g. Sb₂O₃, are added and subsequently they are mixed well. The glass mixture is melted into a continuous melting aggregate at ca. 1150° C., then fined (1200° C.) and homogenized. At a casting temperature of about 1180° C., the glass can be cast and processed to the desired dimensions. Experience has shown that in the continuous aggregate of a high volume, the temperatures can be reduced for at least ca. 100 K and the material can be processed by the pressing method close to the final geometry. TABLE 1 Melting example for 100 kg of calculated glass (according to example 10) Oxide % by weight Raw material Weight (g) SiO₂ 3.69 SiO₂ 3686.90 B₂O₃ 20.00 H₃BO₃ 35469.99 ZnO 17.20 ZnO 17164.71 Al₂O₃ 1.00 Al(OH)₃ 1547.16 Li₂O 0.88 LiNO₃ 4052.58 1.00 Li₂CO₃ 2482.46 Nb₂O₅ 4.21 Nb₂O₅ 4209.78 La₂O₃ 28.52 La₂O₃ 28462.62 Ta₂O₅ 16.00 Ta₂O₅ 15965.33 Y₂O₃ 4.50 Y₂O₅ 4491.22 ZrO₂ 3.00 ZrO₂ 2998.04 Sb₂O₃ 0.20 Sb₂O₃ 200.33 Sum 100.20 120731.12

The properties of the glass thus obtained are given in table 3 as example 10.

Example 2

Tables 2 to 5 comprise the examples 1 to 26 according to the present invention.

All glasses according to the present invention have a Tg of lower than or equal to 560° C., have a very good alkali resistance and can be processed well. The color code of the glasses according to the present invention achieves a value of up to 38/32. TABLE 2 Examples 1 to 6 (data based on oxide in % by weight, n.d. means “not detected”): Exp. 1 2 3 4 5 6 SiO₂ 4.79 4.79 4.99 4.69 4.69 3.69 B₂O₃ 19.89 19.89 19.89 19.89 19.89 19.89 ZnO 19.46 19.5 18.46 18.96 18.96 18.96 Al₂O₃ 1.00 Li₂O 1.88 1.88 1.88 1.88 1.88 1.88 Nb₂O₅ 1.77 2.77 3.77 2.27 3.77 3.77 La₂O₃ 28.32 28.32 28.52 28.52 28.52 28.52 Ta₂O₅ 18.98 15.98 16.08 16.38 16.38 16.38 Y₂O₃ ZrO₂ 4.91 6.91 6.41 7.41 5.91 5.91 Sb₂O₃ +UZ,24/27 0.20 0.20 0.20 Σ 100.0 100.0 100.0 100.2 100.2 100.2 La₂O₃ + ZrO₂ + Nb₂O₅ + 54.0 54.0 54.8 54.6 54.6 54.6 Ta₂O₅ + Y₂O₃ + HfO₂ Σ R₂O (Alkalies) 1.88 1.88 1.88 1.88 1.88 1.88 Σ RO (Alkaline-earths) Σ B₂O₃, ZnO 39.35 39.35 38.35 38.85 38.85 38.85 Σ Al₂O₃, Y₂O₃, WO₃, 4.91 6.91 6.41 7.41 5.91 6.91 TiO₂, ZrO, HfO₂, R₂O Properties τ_(i) (10 mm, 400 nm) 0.98 0.97 0.96 0.97 0.96 0.96 τ_(i) (10 mm, 500-550 nm) >=0.994 >=0.991 >=0.994 >=0.99 >=0.994 >=0.993 Color code 38/31 40/31 39/31 38/31 42/32 42/31 n_(d) (7K/h) 1.80159 1.80490 1.80790 1.80592 1.80879 1.81066 v_(d) (7K/h) 41.54 41.24 40.80 41.35 40.68 40.56 Pg, F 0.5651 0.5655 0.5667 0.5654 0.5672 0.5669 ΔP_(g,F) −0.0088 −0.0089 −0.0085 −0.0089 −0.0082 −0.0087 α_((20-300° C.)) [10⁻⁶/K] 7.09 7.12 7.09 7.12 7.07 7.10 Tg [° C.] 533 536 536 540 541 538 ρ[g/cm³] 4.59 4.55 4.5427 4.561 4.559 4.574 ΔT = [T(η = 10^(7.6)) − T(η = 10¹³ dPas)] 94 SR 51.0 51.3 AR 1.2 1.0

TABLE 3 Examples 7 to 13 (data based on oxide in % by weight) Exp. 7 8 9 10 11 12 13 SiO₂ 3.69 3.69 3.70 3.69 4.19 4.69 3.69 B₂O₃ 19.89 20.00 20.00 20.00 20.00 20.00 20.00 ZnO 18.96 19.20 19.20 17.20 16.20 18.20 15.70 Al₂O₃ 1.00 1.00 1.00 1.00 1.00 1.00 1.00 Li₂O 1.88 1.88 2.00 1.88 1.88 1.88 1.88 Nb₂O₅ 3.77 4.21 4.50 4.21 4.21 6.21 4.21 La₂O₃ 28.52 28.52 30.60 28.52 28.52 26.52 28.52 Ta₂O₅ 16.38 16.00 16.00 16.00 16.00 16.00 16.00 Y₂O₃ 2.00 2.50 3.00 4.50 5.00 2.50 6.00 ZrO₂ 3.91 3.00 — 3.00 3.00 3.00 3.00 Sb₂O₃ 0.20 0.20 0.20 0.20 0.20 0.20 0.20 Σ 100.2 100.20 100.00 100.20 100.20 100.20 100.20 La₂O₃ + ZrO₂ + Nb₂O₅ + 54.6 54.2 54.1 56.2 56.7 54.2 57.7 Ta₂O₅ + Y₂O₃ + HfO₂ Σ R₂O (Alkalies) 1.88 1.88 2.00 1.88 1.88 1.88 1.88 Σ RO (Alkaline-earths) Σ B₂O₃, ZnO 38.85 39.20 39.20 37.20 36.20 38.20 35.70 Σ Al₂O₃, Y₂O₃, WO₃, 6.91 6.50 4.00 8.50 9.00 6.50 10.00 TiO₂, ZrO, HfO₂, R₂O Properties τ_(i) (10 mm, 400 nm) 0.96 0.96 0.95 0.96 0.95 0.96 0.96 τ_(i) (10 mm, 500-550 nm) >=0.992 >=0.995 >=0.987 0.995 0.98 >=0.985 >=0.98 Color code 42/31 38/32 42/31 42/31 42/31 42/31 42/31 n_(d) (7K/h) 1.80663 1.80517 1.80109 1.80774 1.80563 1.80472 1.80835 v_(d) (7K/h) 41.02 41.04 41.47 41.21 41.40 40.15 41.39 Pg, F 0.5665 0.5667 0.5665 0.5662 0.5665 0.5687 0.5658 ΔP_(g,F) −0.0083 −0.0081 −0.0075 −0.0083 −0.0077 −0.0075 −0.0084 α_((20-300° C.)) [10⁻⁶/K] 7.25 7.27 7.48 7.33 7.30 7.06 7.42 Tg [° C.] 533 532 529 544 545 540 546 ρ [g/cm³] 4.57 4.56 4.57 4.5659 4.5452 4.4827 4.560 ΔT = [T(η = 10^(7.6)) − T(η = 10¹³ dPas)] 93 95 96 SR 51.3 AR 1.0

TABLE 4 Examples 14 to 20 (data based on oxide in % by weight) Exp. 14 15 16 17 18 19 20 SiO₂ 3.69 3.69 3.69 3.19 3.69 3.40 3.57 B₂O₃ 20.00 20.00 20.00 20.00 20.00 18.80 20.00 ZnO 16.20 14.70 14.70 16.20 17.20 18.40 19.10 Al₂O₃ 0.50 0.50 0.30 1.00 1.00 1.08 1.02 Li₂O 1.88 1.88 2.08 1.88 1.88 1.79 1.65 Nb₂O₅ 4.21 4.21 4.21 4.21 4.21 4.06 14.50 La₂O₃ 28.52 28.52 28.52 28.52 28.52 31.60 18.70 Ta₂O₅ 16.00 16.00 16.00 16.00 18.00 15.60 15.80 Y₂O₃ 6.00 7.50 7.50 6.00 2.50 2.40 2.47 ZrO₂ 3.00 3.00 3.00 3.00 3.00 2.90 2.97 Sb₂O₃ 0.20 0.20 0.20 0.20 0.20 0.17 0.17 Σ 100.2 100.2 100.2 100.2 100.2 100.2 100 La₂O₃ + ZrO₂ + Nb₂O₅ + 57.7 59.2 59.2 57.7 56.2 56.6 54.4 Ta₂O₅ + Y₂O₃ + HfO₂ Σ R₂O (Alkalies) 1.88 1.88 2.08 1.88 1.88 1.79 1.65 Σ RO (Alkaline-earths) — — — — — — — Σ B₂O₃, ZnO 36.20 34.70 34.70 36.20 37.20 37.20 39.10 Σ Al₂O₃, Y₂O₃, 9.50 11.00 10.80 10.00 6.50 6.38 6.46 WO₃, TiO₂, ZrO, HfO₂, R₂O Properties T_(i) (10 mm, 400 nm) 0.96 0.96 n.d. 0.96 n.d. 0.98 85 T_(i) (10 mm, 500-550 nm) >=0.99 >=0.98 n.d. >=0.99 n.d. >=0.995 >=92 Color code 42/31 42/31 n.d. 42/31 n.d. 38/32 48/33 n_(d) (7K/h) 1.81043 1.81213 1.81153 1.80894 1.81066 1.81138 1.82953 v_(d) (7K/h) 41.29 41.41 41.43 40.69 40.12 41.22 35.42 Pg, F 0.5662 0.566 0.5657 0.5674 0.5682 0.5674 0.5795 ΔP_(g,F) −0.0082 −0.0082 −0.0084 −0.008 −0.0082 −0.0070 −0.0048 α_((20-300° C.)) [10⁻⁶/K] 7.44 7.49 7.62 7.23 7.11 7.44 6.66 Tg [° C.] 543 546 543 540 536 540 534 ρ [g/cm³] 4.5797 4.5795 4.5765 4.5831 4.6054 4.39970 4.3997 ΔT = [T(η = 10^(7.6)) − T(η = 10¹³ dPas)] SR 51.2 51.2 AR 1.0 1.0

TABLE 5 Examples 21 to 26 (data based on oxide in % by weight) Exp. 21 22 23 24 25 26 SiO₂ 3.60 3.45 1.91 3.70 3.79 3.70 B₂O₃ 19.53 18.69 21.28 20.05 20.54 20.08 Al₂O₃ 0.98 0.94 0.15 Li₂O 1.90 1.89 1.93 1.39 Na₂O 3.81 0.52 K₂O 5.54 0.79 Cs₂O 2.24 Nb₂O₅ 4.11 3.93 8.23 4.22 2.05 4.22 La₂O₃ 27.95 24.12 22.02 28.60 29.29 28.64 Ta₂O₅ 15.67 21.84 23.67 16.04 16.43 16.06 Y₂O₃ 2.45 2.51 0.64 2.51 HfO₂ 0.54 MgO 1.12 CaO 0.55 0.57 SrO 1.78 BaO ZnO 18.76 17.94 15.07 19.24 19.71 19.28 ZrO₂ 2.93 2.80 2.38 3.00 3.08 1.47 TiO₂ 1.00 Sb₂O₃ 0.20 0.20 0.20 0.20 0.20 0.20 Σ 100.0 100.0 100.0 100.0 100.0 100.0 La₂O₃ + ZrO₂ + Nb₂O₅ + 53.1 53.2 56.3 54.4 51.5 52.9 Ta₂O₅ + Y₂O₃ + HfO₂ Σ R₂O (Alkalies) 3.8 5.5 4.1 1.9 1.9 2.7 Σ RO (Alkaline-earths) 0.0 0.0 1.1 0.5 2.3 0.0 Σ B₂O₃, ZnO 38.3 36.6 36.3 39.3 40.2 39.4 Σ Al₂O₃, Y₂O₃, 10.2 9.8 6.5 7.4 5.6 7.8 WO₃, TiO₂, ZrO, HfO₂, R₂O Properties T_(i) (10 mm, 400 nm) 0.96 0.64 0.88 0.95 T_(i) (10 mm, 500-550 nm) 0.992 0.729 0.922 0.99 Color code 38/31 44/34 37/31 39/33 n_(d) (7K/h) 1.78203 1.76629 1.81504 1.80842 1.79501 1.80156 v_(d) (7K/h) 40.61 39.10 37.06 40.97 42.36 39.97 P_(g,F) 0.5674 0.5704 0.5751 0.5669 0.5642 0.5698 ΔP_(g,f) −0.0081 −0.0077 −0.0064 −0.0080 −0.0083 −0.0068 α_((20-300° C.)) [10⁻⁶/K] 7.68 7.43 6.95 7.4 7.6 7.45 Tg [° C.] 545 548 522 526 531 524 ρ [g/cm³] 4.4613 4.3805 4.5341 4.5773 4.5590 4.5170 ΔT = (T(logη = 10^(7.6)) − 93 94 98 T(logη10¹³)) [K] SR [class] (ISO 8424) AR [class] (ISO 10629) 

1. A lead and arsenic free optical glass having a refractive index n_(d) of 1.75≦n_(d)≦1.83 and an Abbe number v_(d) of 34≦v_(d)≦44, characterized in that the glass comprises the following composition (based on oxide in % by weight): SiO₂ 0.5-8   B₂O₃ 10-25 ZnO 10-26 La₂O₃ 18-34 Ta₂O₅ >15-25   Nb₂O₅ 0.5-15  WO₃  0-10 Al₂O₃ 0-2 Li₂O 0-5 Na₂O 0-6 K₂O 0-8 Cs₂O 0-9 MgO 0-5 CaO 0-5 SrO 0-5 BaO 0-5 Y₂O₃  0-10 TiO₂ 0-6 ZrO₂  0-11 HfO₂ 0-6 Σ B₂O₃, ZnO 30-45 Σ Alkali oxides  0-10 Σ Alkaline-earth oxides 0-8 Σ Al₂O₃, Y₂O₃, WO₃, TiO₂,  0-15 ZrO₂, HfO₂, Alkaline-earth oxides Conventional refining agents 0-2


2. A lead and arsenic free optical glass having a refractive index n_(d) of 1.75≦n_(d)≦1.83 and an Abbe number v_(d) of 34≦v_(d)≦44, characterized in that the glass comprises the following composition (based on oxide in % by weight): SiO₂ 0.5-8   B₂O₃ 10-25 ZnO 10-26 La₂O₃ 18-34 Ta₂O₅ >15-25   Nb₂O₅ 0.5-15  Al₂O₃ 0-2 Li₂O 0.1-4   Na₂O 0-6 K₂O 0-8 Cs₂O 0-9 MgO 0-5 CaO 0-5 SrO 0-5 BaO 0-5 Y₂O₃  0-10 TiO₂ 0-6 ZrO₂  0-11 HfO₂ 0-6 Σ B₂O₃, ZnO 30-45 Σ Alkali oxides 0.1-10  Σ Alkaline-earth oxides 0-8 Σ Al₂O₃, Y₂O₃, WO₃, TiO₂,  0-15 ZrO₂, HfO₂, Alkaline-earth oxides Conventional refining agents 0-1


3. The glass according to claim 1, wherein the sum of La₂O₃+Ta₂O₃+Nb₂O₃+Y₂O₃+ZrO₂ is higher than 50% by weight based on oxide.
 4. The glass according to claim 1, which comprises the following composition (based on oxide in % by weight): SiO₂ 1-7 B₂O₃ 15-24 ZnO 12-24 La₂O₃ 23-33 Ta₂O₅ 15.5-23   Nb₂O₅ 1-8 WO₃ 0-5 Al₂O₃   0-1.5 Li₂O 0.1-4   Na₂O 0-5 K₂O 0-6 Cs₂O 0-8 MgO 0-4 CaO 0-4 SrO 0-4 BaO 0-4 Y₂O₃ 0-9 TiO₂ 0-3 ZrO₂  1-10 HfO₂ 0-3 Σ B₂O₃, ZnO 34-42 Σ La₂O₃, Ta₂O₃, Nb₂O₅, Y₂O₃, ZrO₂ >50 Σ Alkali oxides 0-7 Σ Alkaline-earth oxides 0-5 Σ Al₂O₃, Y₂O₃, WO₃, TiO₂, ZrO₂,  0-13 HfO₂, Alkaline-earth oxides Conventional refining agents 0-2


5. The glass according to claim 1, which comprises the following composition (based on oxide in % by weight): SiO₂ 1-7 B₂O₃ 15-23 ZnO 12-24 La₂O₃ 23-33 Ta₂O₅ 15.5-23   Nb₂O₅ 1-8 WO₃ 0-5 Al₂O₃   0-1.5 Li₂O 0.5-4   Na₂O 0-4 K₂O 0-4 Cs2O 0-4 MgO 0-4 CaO 0-4 SrO 0-4 BaO 0-4 Y₂O₃ 0-9 TiO₂ 0-3 ZrO₂  1-10 HfO₂ 0-3 Σ B₂O₃, ZnO 38-41 Σ La₂O₃, Ta₂O₃, Nb₂O₅, >50 Y₂O₃, ZrO₂ Σ Alkali oxides 0-6 Σ Alkaline-earth oxides 0-4 Σ Al₂O₃, Y₂O₃, WO₃, TiO₂,  0-13 ZrO₂, HfO₂, Alkaline-earth oxides Conventional refining agents 0-2


6. The glass according to claim 1, containing, as a refining agent, at least one of the following components (in % by weight): Sb₂O₃ 0 to 1 and/or SnO 0 to 1 and/or SO₄ ²⁻ 0 to 1 and/or F  0 to
 1.


7. The glass according to claim 1, which is gadolinium-free and/or fluorine-free.
 8. An optical element for use in the fields of mapping, telecommunication, optical communication engineering, projection, mobile drive and/or laser technology, said optical element comprising a glass according to claim
 1. 9. A method of producing an optical element, said method comprising the step of precise pressing a glass according to claim
 1. 